Metal-substituted transistor gates

ABSTRACT

One aspect of this disclosure relates to an integrated circuit structure. An integrated circuit structure embodiment includes a substrate, a gate dielectric over the substrate, a carbon structure having a predetermined thickness in contact with and over the gate dielectric, and a layer of desired gate material for a transistor in contact with and over the carbon structure. The layer of desired gate material includes a predetermined thickness corresponding to the predetermined thickness of the carbon structure to support a metal substitution process to replace the carbon structure with the desired gate material. Other aspects and embodiments are provided herein.

This application is a divisional of U.S. application Ser. No.11/176,738, filed Jul. 7, 2005, which is incorporated herein byreference.

TECHNICAL FIELD

This disclosure relates generally to integrated circuits, and moreparticularly, to transistor structures and methods of formation.

BACKGROUND

Many integrated circuits include a metal-oxide-semiconductor,field-effect transistor, or “MOSFET” for short, which includes a gate, asource, a drain, and a body. An issue in MOSFET design involves thestructure and composition of its gate. Some early MOSFET designsincluded aluminum gates, and later MOSFET designs used polysilicon gatesbecause of the desire for a self-aligned gate as well as the tendency ofaluminum to diffuse through the underlying insulative layer and alsobecause of problems that the relatively low melting temperature ofaluminum caused with annealing processes. Polysilicon can be doped toact as a conductor, but with significantly more electrical resistancethan aluminum. This higher resistance can be ameliorated somewhat bysilicidation. However, the higher resistance of even the salicidedpolysilicon gates combines with inherent integrated-circuit capacitancesto cause significant delays in conducting signals from one circuit pointto another, ultimately limiting how fast integrated circuits operate.

Currently, the semiconductor industry relies on the ability to reduce orscale the dimensions of its basic devices, including the gatedielectric, of its transistor devices to obtain lower power consumptionand higher performance. To reduce transistor size, the thickness of thegate dielectric is reduced in proportion to the shrinkage of the gatelength. Increased scaling and other requirements in microelectronicdevices have created the need to use other dielectric materials as gatedielectrics, in particular dielectrics with higher dielectric constants(k) to replace the conventional use of various combinations of SiO₂,Si₃N₄ and SiON. Practical higher dielectric constant (k) materials havethe properties of high permittivity, thermal stability, high film andsurface quality and smoothness, low hysteresis characteristics, lowleakage current density, and long term reliability. However, polysilicongates and high-k dielectric materials have interface instability issues.

BRIEF DESCRIPTION OF THE DRAWINGS

FIGS. 1A-1E illustrate a process for forming a metal substituted gatefor a transistor structure, according to various embodiments of thepresent subject matter.

FIG. 2 illustrates an embodiment of a metal gate substitution technique.

FIG. 3 illustrates a wafer, upon which the transistors with metalsubstituted gates can be fabricated according to embodiments of thepresent subject matter.

FIG. 4 illustrates a simplified block diagram of a high-levelorganization of an electronic system that includes the transistor withthe metal-substituted gate, according to various embodiments.

FIG. 5 illustrates a simplified block diagram of a high-levelorganization of an electronic system that includes transistors withmetal substituted gates, according to various embodiments.

DETAILED DESCRIPTION

The following detailed description refers to the accompanying drawingswhich show, by way of illustration, specific aspects and embodiments inwhich the present invention may be practiced. The various embodimentsare not necessarily mutually exclusive, as aspects of one embodiment canbe combined with aspects of another embodiment. Other embodiments may beutilized and structural, logical, and electrical changes may be madewithout departing from the scope of the present invention. In thefollowing description, the terms wafer and substrate are usedinterchangeably to refer generally to any structure on which integratedcircuits are formed, and also to such structures during various stagesof integrated circuit fabrication. Both terms include doped and undopedsemiconductors, epitaxial layers of a semiconductor on a supportingsemiconductor or insulating material, combinations of such layers, aswell as other such structures that are known in the art. The terms“horizontal” and “vertical”, as well as prepositions such as “on”,“over” and “under” are used in relation to the conventional plane orsurface of a wafer or substrate, regardless of the orientation of thewafer or substrate. References to “an”, “one”, or “various” embodimentsin this disclosure are not necessarily to the same embodiment, and suchreferences contemplate more than one embodiment. The following detaileddescription is, therefore, not to be taken in a limiting sense, and thescope of the present invention is defined only by the appended claims,along with the full scope of equivalents to which such claims areentitled.

One aspect of this disclosure relates to a method for forming atransistor. According to various method embodiments, a gate dielectricis formed on a substrate, a substitutable structure is formed on thegate dielectric, and source/drain regions for the transistor are formed.A desired gate material is substituted for the starting or substitutablestructure to provide the desired gate material on the gate dielectric.Some embodiments use carbon for the substitutable material. Variousembodiments replace carbon starting material with gold (Au), silver(Ag), gold alloy, silver alloy, copper (Cu), platinum (Pt), rhenium(Re), ruthenium (Ru), rhodium (Rh), nickel (Ni), osmium (Os), palladium(Pd), iridium (Ir), cobalt (Co), and germanium (Ge). Some embodimentsuse silicon, germanium or silicon-germanium for the starting orsubstitutable material. Various embodiments replace silicon, germaniumor silicon-germanium starting material with aluminum, copper, silver,gold, alloys of silver, or alloys of gold. Some embodiments form ahigh-k gate dielectric, such as may be formed by an atomic layerdeposition process, an evaporated deposition process, and a metaloxidation process. According to various embodiments, the high-k gatedielectric includes one or more of the following: AlO_(X), LaAlO₃,HfAlO₃, Pr₂O₃-based lanthanide oxide, HfSiON, Zr—Sn—Ti—O, ZrON, HFO₂/Hf,ZrAl_(X)O_(Y), ZrTiO₄, Zr-doped Ta, HfO₂—Si₃N₄, lanthanide oxide,TiAlO_(X), LaAlO_(X), La₂Hf₂O₇, HfTaO amorphous lanthanide doped TiOx,TiO₂, HfO₂, CrTiO₃, ZrO₂, Y₂O₃, Gd₂O₃, praseodymium oxide, amorphousZrO_(X)N_(Y), Y—Si—O, LaAlO₃, amorphous lanthanide-doped TiO_(X),HfO₂/La₂O₃ nanolaminates, La₂O₃/Hf₂O₃ nanolaminates, HfO₂/ZrO₂nanolaminates, lanthanide oxide/zirconium oxide nanolaminates,lanthanide oxide/hafnium oxide nanolaminates, TiO₂/CeO₂ nanolaminates,PrO_(X)/ZrO₂ nanolaminates, Hf₃N₄/HfO₂ nanolaminates, and Zr₃N₄/ZrO₂nanolaminates. Other aspects and embodiments are provided herein.

Disclosed herein, among other things, is a transistor device structurewith substituted metal gates. Various embodiments provide thesubstituted metal gates over and in contact with a high-k dielectric.Those of skill in the art will understand that the term high-kdielectric refers to a dielectric material having a dielectric constantgreater than that of silicon dioxide. That is, a high-k dielectric has adielectric constant greater than 4. A transistor device structure with ahigh-k gate dielectric and a substituted metal gate increases thecapacitance and reduces the resistance of integrated circuits, which isuseful for nanoscale integrated circuits. Additionally, the transistordevice disclosed herein is capable of being manufactured with gatesengineered to have differing work functions. Thus, in CMOS designs, atransistor metal gate is able to provide a desired work function (within0.2 eV of the E_(C) of silicon) for NMOS devices and a desired workfunction (within 0.2 eV of the E_(V) of silicon) for PMOS devices.

The substituted metal gates replace a substitutable material formed on agate dielectric. Various embodiments provide a substituted gate wherethe starting material is a mixture of silicon and germanium over theentire range of silicon and germanium from 0 to 100 percent silicon.Various embodiments replace the silicon, germanium or silicon-germaniumstarting material with aluminum, copper, silver, gold, alloys of silver,or alloys of gold. As the silicon-germanium phase relationship is one ofa continuous series of solid solutions, the metal substitution ofaluminum, silver or gold will work with all mixtures of silicon andgermanium. Various embodiments provide a substituted gate where thestarting material is carbon. Various embodiments replace the carbonstarting material with gold (Au), silver (Ag), gold alloy, silver alloy,copper (Cu), platinum (Pt), rhenium (Re), ruthenium (Ru), rhodium (Rh),nickel (Ni), osmium (Os), palladium (Pd), iridium (Ir), cobalt (Co), andgermanium (Ge).

Gold and silver may be substituted for carbon. However, gold and silverare not able to be substituted for all ranges of carbon-silicon orcarbon-germanium alloys. Carbon and germanium are not soluble, such thatthe solid phase is a two phase material. The melting point of carbon(3828° C.) is much higher than that of germanium (938° C.). Thus, alloyswith significant amounts of carbon may provide a problem. Silicon andcarbon are insoluble and have an intermetallic compound SiC (siliconcarbide) as it forms peritectoidly at 2545° C., while the eutectictemperature between silicon and silicon carbide is at 1404° C. Thus, itappears unlikely that one could replace silicon carbide in a siliconrich starting material. However, in a carbon rich silicon carbidematerial that is properly formed, the temperature of the material couldbe raised to just under 2545° C. without forming a liquid phase. Thus,it appears that an alloy having above 50 atomic percent carbon is apossible candidate.

Various embodiments provide the substituted gate on a high-k dielectric,such as AlO_(X), LaAlO₃, HfAlO₃, Pr₂O₃-based lanthanide oxide, HfSiON,Zr—Sn—Ti—O, ZrON, HfO₂/Hf, ZrAl_(X)O_(Y), ZrTiO₄, Zr-doped Ta,HfO₂—Si₃N₄, lanthanide oxide, TiAlO_(X), LaAlO_(X), La₂Hf₂O₇, HfTaOamorphous lanthanide doped TiOx, TiO₂, HfO₂, CrTiO₃, ZrO₂, Y₂O₃, Gd₂O₃,praseodymium oxide, amorphous ZrO_(X)N_(Y), Y—Si—O, LaAlO₃, amorphouslanthanide-doped TiO_(X), HfO₂/La₂O₃ nanolaminates, La₂O₃/Hf₂O₃nanolaminates, HfO₂/ZrO₂ nanolaminates, lanthanide oxide/zirconium oxidenanolaminates, lanthanide oxide/hafnium oxide nanolaminates, TiO₂/CeO₂nanolaminates, PrO_(X)/ZrO₂ nanolaminates, Hf₃N₄/HfO₂ nanolaminates, andZr₃N₄/ZrO₂ nanolaminates.

Device Structure

FIGS. 1A-1E illustrate a process for forming a metal substituted gatefor a transistor structure, according to various embodiments of thepresent subject matter. FIG. 1A illustrates a substrate 101 and shallowtrench isolation (STI) regions 102. The substrate 101 can be asemiconductor wafer as well as structures having one or more insulative,semi-insulative, conductive, or semiconductive layers and materials.Thus, for example, the substrate can include silicon-on-insulator,silicon-on-sapphire, and other structures upon which semiconductordevices are formed.

FIG. 1B further illustrates a gate dielectric layer 103 formed on thesubstrate 101, and a gate substitutable layer 104 formed on the gatedielectric layer 103. According to some embodiments, the gate dielectriclayer includes a silicon oxide, such as silicon dioxide. In variousembodiments, the gate dielectric layer includes a high-k dielectric,such as AlO_(X), LaAlO₃, HfAlO₃, Pr₂O₃-based Lanthanide Oxide, HfSiON,Zr—Sn—Ti—O, ZrON, HfO₂/Hf, ZrAl_(X)O_(Y), ZrTiO₄, ZR-doped Ta,HfO₂—Si₃N₄, lanthanide oxide, TiAlO_(X), LaAlO_(X), La₂Hf₂O₇, HfTaOamorphous lanthanide doped TiOx, TiO₂, HfO₂, CrTiO₃, ZrO₂, Y₂O₃, Gd₂O₃,praseodymium oxide, amorphous ZrO_(X)N_(Y), Y—Si—O, LaAlO₃, amorphouslanthanide-doped TiO_(X), HfO₂/La₂O₃ nanolaminates, La₂O₃/Hf₂O₃nanolaminates, HfO₂/ZrO₂ nanolaminates, lanthanide oxide/zirconium oxidenanolaminates, lanthanide oxide/hafnium oxide nanolaminates, TiO₂/CeO₂nanolaminates, PrO_(X)/ZrO₂ nanolaminates, Hf₃N₄/HfO₂ nanolaminates,Zr₃N₄/ZrO₂ nanolaminates, and the like. The use of the high-k dielectricincreases the capacitance, which is useful for nanoscale integratedcircuits. As will be described in more detail below, the material of thegate substitutable layer 104 is selected with respect to the desiredgate material, to allow the gate material to replace the gatesubstitutable layer to form a gate of the desired gate metal where thesubstitutable material was positioned on the gate dielectric.

As illustrated in FIG. 1C, portions of the gate dielectric layer 103 andthe gate substitutable layer 104 are removed to define a gate 105, andsidewalls or spacers 106 are formed along the gate 105. Source/drainregions are also formed. The source/drain regions 107 can be formedusing conventional ion implantation and subsequent annealing. Theseannealing temperatures can pose problems for aluminum gates and othermetal gates that have melting temperatures less than the annealtemperature for the source/drain regions.

With reference to FIG. 1D, an insulative fill layer 108 is provided tomatch the thickness of the gate stack. A planarization procedure, suchas chemical-mechanical polishing, can be used to provide an even surfaceacross the fill layer 108 and the gate substitutable layer 104. A metallayer 109 formed of material intended to be the gate material isdeposited over the gate substitutable layer 104 and the fill layer 108.The metal layer 109 is also referred to herein as a layer of gatematerial. Various deposition processes, such as evaporation, sputteringor chemical vapor deposition, may be used to form the metal layer 109.The volume of layer 109 is significantly larger than the volume of thesubstitutable material left on the wafer.

After the metal layer 109 is deposited on the gate substitutable layer,a metal-substitution reaction is induced. The reaction can be providedby annealing the structure in a non-oxidizing atmosphere such as anitrogen gas or a forming gas. The heating urges diffusion ordissolution of the intended gate material in metal layer 109 for thesubstitutable material 104. The substitution process is bounded by thespacers 106 and the gate dielectric 103.

At the conclusion of the substitution reaction, the method removes theresidual metal of layer 109 and the substitutable material, such as maybe achieved using conventional planarization. FIG. 1E shows theresulting low-resistance gate structure. The illustrated structureincludes a metal substituted gate 110 formed by the substitution of themetal of layer 109. The metal substituted gate 110 may include a smallamount of the gate substitutable material which did not diffuse abovethe planarization level 111. Such small amounts of the gatesubstitutable material do not significantly affect the conductivity ofthe metal substituted gate 110, and thus do not significantly affect theperformance of the device.

Drain and source contacts (not shown) can be formed, as well asinterconnects to other transistors or components, using conventionaltechniques. Another heat treatment may occur after packaging theintegrated circuit in a protective housing in an attempt to minimize theresistivity of the metal gate contacts and other metal interconnections.

The metal gate substitution technique, as disclosed herein, can beapplied to MOS devices, as generally illustrated in FIG. 1, as well asto form metal floating gates and/or metal control gates in nonvolatiledevices. Additionally, various high-k dielectrics can be used betweenthe floating gate and the substrate, and between the control gate andthe floating gate in these nonvolatile devices.

Metal Gate Substitution Technique

FIG. 2 illustrates an embodiment of a metal gate substitution technique.At 212; a gate dielectric is formed on a substrate. The gate dielectricincludes a high-k dielectric in some embodiments. Various high-kdielectric embodiments are identified below. At 213, a layer of gatesubstitutable material is formed on the gate dielectric. Examples ofgate substitutable material include polysilicon, germanium,silicon-germanium and carbon. At 214, source/drain regions are formed. Alayer of gate material, also referred to herein as a metal layer, isformed at 215 on the gate substitutable material. Examples of suchmetals include gold, silver, and aluminum. Other metals may be used. At216, the gate material is substituted for the layer of gatesubstitutable material.

A metal substitution reaction substitutes or replaces the substitutablematerial (e.g. silicon, germanium, silicon-germanium, carbon) with ametal. After the substitution, the resulting gate structure includessubstantially all of the desired metal. Small amounts of thesubstitutable material may remain in the gate structure. Thesubstitution reaction can be induced by heating the integrated circuitassembly to a desired temperature in a vacuum, nitrogen, argon, forminggas or other nonoxidizing atmosphere. Heating causes diffusion of themetal layer 109 into the substitutable layer. The annealing temperaturefor the substitution is less than the eutectic (lowest melting)temperature of materials involved in the substitution for the reactionfor substitution to occur. For example, to form a gold gate, one couldform the metal layer from gold and anneal at approximately 300° C. tosubstitute the gold for a silicon substitutable structure, and to form asilver gate one could form the metal layer from silver and anneal atapproximately 500-600° C. to substitute the silver for the siliconsubstitutable structure. A polysilicon and germanium substitutablematerial can be used, which reduces the anneal temperature.

According to various embodiments, the gate substitutable material 104shown in FIGS. 1A-1E includes polysilicon. In some embodiments, the gatesubstitutable material includes germanium. Some embodiments usesilicon-germanium, with any percentage of silicon in the range of 0% to100% as the gate substitutable material 104. Some embodiments use carbonas the gate substitutable material 104.

With respect to embodiments which use polysilicon, germanium orsilicon-germanium as the gate substitutable material 104, someembodiments use aluminum as the replacement metal for the substitutedgate, some embodiments use silver as the replacement metal, someembodiments use gold as the replacement metal, some embodiments use analloy of silver as the replacement metal, and some embodiments use analloy of gold as the replacement metal.

With respect to embodiments which use carbon as the gate substitutablematerial 104, some embodiment use gold as the replacement metal for thesubstituted gate, some embodiments use silver as the replacement metal,some embodiments use an alloy of gold as the replacement metal, someembodiments use an alloy of silver as the replacement metal, someembodiments use copper as the replacement metal, some embodiments useplatinum as the replacement metal, some embodiments use rhenium as thereplacement metal, some embodiments use ruthenium as the replacementmetal, some embodiments use rhodium as the replacement metal, someembodiments use nickel as the replacement metal, some embodiments useosmium as the replacement metal, some embodiments use palladium as thereplacement metal, some embodiments use iridium as the replacementmetal, some embodiments use cobalt as the replacement metal, and someembodiments use germanium as the replacement metal.

Table 1 provides a listing of various embodiments for substituted metalgates formed using various substitutable or starting material andvarious metal gate material. Table 1 also identifies the eutectic(lowest melting) temperature of the elements, including both thesubstitutable material and the metal gate material, involved in thesubstitution process, and the approximate ranges of annealingtemperatures that are used in various method embodiments to perform themetal substitution reaction. The identified substitution temperaturesare approximate, as they depend on process control tolerances and theeffect of impurities. Substitution may occur at other temperatures thanthat provided as an example in the table. TABLE 1 APPROXIMATEAPPROXIMATE SUBSTITUTION SUB- EUTECTIC TEMPERATURE STITUTABLE GATETEMPERATURE RANGE MATERIAL MATERIAL ° C. ° C. Silicon Aluminum  577450-525 Silver  835 700-800 Gold  363 250-325 Alloys of Silver * **Alloys of Gold * ** Germanium Aluminum  420 275-325 Silver  653 500-600Gold  361 250-325 Alloys of Silver * ** Alloys of Gold * ** Silicon-Aluminum  <420*  300-375** Germanium Silver  <653*  475-575** Gold <361*  250-300** Alloys of Silver * ** Alloys of Gold * ** Carbon Gold1060  925-1025 Silver***  962 825-925 Alloys of Gold * ** Alloys ofSilver * ** Copper*** 1100  900-1025 Platinum 1705 1500-1625 Rhenium2505 2300-2450 Ruthenium 1940 1775-1875 Rhodium 1694 1525-1625 Nickel1326 1150-1275 Osmium 2732 2400-2600 Palladium 1504 1300-1425 Iridium2296 2050-2200 Cobalt 1320 1150-1275 Germanium  938 775-875*Ternary diagrams (e.g. Si—Ge—Al phase diagram; Si—Ge—Ag phase diagram;Si—Ge—Au phase diagram) can be used to determine these eutectictemperatures. With respect to the Si—Ge system, silicon and germaniumare completely soluble in each other in the solid phase. Thus, there isa possibility that there is a lower melting point in the ternary systemthan in the binary systems.**The substitution temperature of ternary systems, as well as the othersystems provided herein, can be established by estimating thesubstitution temperature based on the constituent elements and/or byexperiment. The substitution temperatures are less than the eutectictemperatures with some allowance for the effect of any impuritiespresent as well as process control tolerances.***Carbon-Silver and Carbon-Copper systems are shallow pertecticsystems, rather than eutectic systems. It is believed that such shallowpertectic systems can be used to provide the metal gate substitutionprocess.

Various embodiments form an integrated circuit structure using two ormore substitution reactions. Relatively higher temperature substitutionprocesses can be performed before relatively lower temperaturesubstitution processes. For example, a relatively high-temperaturesubstitution reaction with carbon can be performed before a relativelylow-temperature substitution reaction with germanium. Examples ofsubstitution temperature ranges are provided above in Table 1. Thepresent subject matter includes multiple substitution reactionsinvolving various combinations of two or more substitution processesillustrated in Table 1. One application for multiple substitutionreactions is to independently adjust work functions of NMOS and PMOStransistors in CMOS integrated circuits. Multiple substitution reactionsare not limited to this CMOS integrated circuit application.

High-k Dielectric Gate Insulator

As provided above, some embodiments provide the metal substituted gate110 on a high-k gate dielectric 103. Various embodiments use thespecific high-k dielectrics provided below. Some specific processexamples are provided below for the identified high-k dielectric. Theseprocess examples are not intended to be limited to exclude theidentified device structures if the structures are formed using otherprocesses. According to various embodiments, a high-k dielectric can befabricated using atomic layer deposition (ALD) processes, evaporateddeposition processes, and sputtered deposition processes. Additionally,metal can be oxidized to form a high-k dielectric, and the high-kdielectric can be formed as nanolaminates of dielectric material.

Specific chemical formulas are referenced below with respect to varioushigh-k dielectric structures. However, the dielectric structure caninclude stoichiometric structures, non-stoichiometric structures, andcombinations of stoichiometric and non-stoichiometric structures.

AlO_(X)

Various embodiments use an aluminum oxide (AlO_(X)) formed by ALD as ahigh-k dielectric. For example, a pulse of an oxidant can be provided,followed by a purge or evacuation of the oxidant, followed by a pulse ofa precursor containing aluminum, followed by a purge or evacuation ofthe aluminum-containing precursor. The aluminum precursor can include avariety of precursors, such as trimethylaluminum (TMA),trisobutylaluminum (TIBA), dimethylaluminum hydride (DMAH), AlC₃, andother halogenated precursors and organometallic precursors. Oxidants caninclude a water-argon mixture formed by bubbling an argon carrierthrough a water reservoir, H₂O₂, O₂, O₃, and N₂O. The ALD aluminumoxides are not limited to specific aluminum precursors or oxidants.Additional information regarding aluminum oxides formed by ALD can befound in US Patent Application Publication 20030207032A1, entitled“Methods, Systems, and Apparatus for Atomic-Layer Deposition of AluminumOxides in Integrated Circuits,” which is herein incorporated byreference.

LaAlO₃

Various embodiments use a lanthanum aluminum oxide (LaAlO₃) formed byALD as a high-k dielectric. For example, a LaAlO₃ gate dielectric can beformed using atomic layer deposition by employing a lanthanum sequenceand an aluminum sequence, where the lanthanum sequence uses La(thd)₃(thd=2,2,6,6-tetramethyl-3,5-heptanedione) and ozone, and the aluminumsequence uses either trimethylaluminum, Al(CH₃)₃, or DMEAA, an adduct ofalane (AlH₃) and dimethylethylamine [N(CH₃)₂(C₂H₅)], with distilledwater vapor.

A dielectric film containing LaAlO₃, Al₂O₃, and La₂O₃ will have adielectric constant ranging from the dielectric constant of Al₂O₃, 9, tothe dielectric constant of La₂O₃, 30. By controlling the number ofcycles of the lanthanum sequence and the number of cycles of thealuminum sequence, the amount of lanthanum and aluminum deposited on thesurface region of a substrate can be controlled. Thus, a dielectric filmformed by ALD using a lanthanum sequence and an aluminum sequence can beformed with a composition containing selected or predeterminedpercentages of LaAlO₃, Al₂O₃, and La₂O₃, in which case the effectivedielectric constant of the film will be selected or predetermined in therange from 9 to 30. A dielectric film containing almost entirely LaAlO₃will have a dielectric constant in the range of about 21 to about 25.The resulting dielectric containing LaAlO₃ should be amorphous if analuminum sequence is used subsequent to a lanthanum sequence.

In addition to separately controlling the number of cycles of thelanthanum sequence and the aluminum sequence in the ALD process, adielectric film containing LaAlO₃ can be engineered with selectedcharacteristics by also controlling precursor materials for eachsequence, processing temperatures and pressures for each sequence,individual precursor pulsing times, and heat treatment at the end of theprocess, at the end of each cycle, and at the end of each sequence. Theheat treatment may include in situ annealing in various atmospheresincluding argon, nitrogen, and oxygen. A range of equivalent oxidethickness is associated with the capability to provide a compositionhaving a dielectric constant in the range from about 9 to about 30, andthe capability to attain physical film thickness in the range from about0.5 to about 50 nm and above.

Additional information regarding LaAlO₃ dielectric films can be found inUS Patent Application Publication 20030207540A1, entitled “AtomicLayer-Deposited LaAlO₃ Films For Gate Dielectrics,” which is hereinincorporated by reference.

HfAlO

Various embodiments use a hafnium aluminum oxide (HfAlO₃) formed by ALDas a high-k dielectric. For example, an HfAlO₃ gate dielectric can beformed using atomic layer deposition by employing a hafnium sequence andan aluminum sequence, where the hafnium sequence uses HfCl₄ and watervapor, and the aluminum sequence uses either trimethylaluminum,Al(CH₃)₃, or DMEAA, an adduct of alane (AlH₃) and dimethylethylamine[N(CH₃)₂(C₂H₅)], with distilled water vapor.

A dielectric film containing HfAlO₃, Al₂O₃, and HfO₂ has a dielectricconstant ranging from the dielectric constant of Al₂O₃, 9, to thedielectric constant of HfO₂, 25. By controlling the number of cycles ofthe hafnium sequence and the number of cycles of the aluminum sequence,the amount of hafnium and aluminum deposited on the surface region of asubstrate can be controlled. Thus, a dielectric film formed by ALD usinga hafnium sequence and an aluminum sequence can be formed with acomposition containing selected or predetermined percentages of HfAlO₃,Al₂O₃, and HfO₂, in which case the effective dielectric constant of thefilm will be selected or predetermined in the range from 9 to 25.Furthermore, using an aluminum sequence subsequent to a hafniumsequence, the resulting dielectric containing HfAlO₃ should beamorphous.

In addition to separately controlling the number of cycles of thehafnium sequence and the aluminum sequence in the ALD process, adielectric film containing HfAlO₃ can be engineered with selectedcharacteristics by also controlling precursor materials for eachsequence, processing temperatures and pressures for each sequence,individual precursor pulsing times, and heat treatment at the end of theprocess, at the end of each cycle, and at the end of each sequence. Theheat treatment may include in situ annealing in various atmospheresincluding argon and nitrogen.

A range of equivalent oxide thickness, t_(eq) is associated with thecapability to provide a composition having a dielectric constant in therange from about 9 to about 25, and the capability to attain physicalfilm thickness in the range of from about 2 to about 3 nm and above.

Additional information regarding HfAlO₃ dielectric films can be found inUS Patent Application Publication 20030227033A1, entitled “AtomicLayer-Deposited HfAlO₃ Films For Gate Dielectrics,” which is hereinincorporated by reference.

Pr₂O₃-Based La-Oxide

Various embodiments use a Pr₂O₃-based La-Oxide dielectric as a high-kdielectric. For example, a Pr₂O₃-based La-Oxide gate dielectric can beformed by electron beam evaporation as a nanolaminate of Pr₂O₃ and alanthanide oxide selected from the group consisting of Nd₂O₃, Sm₂O₃,Gd₂O₃, and Dy₂O₃.

According to one embodiment, an electron gun generates an electron beamthat hits a target that contains a ceramic Pr₆O₁₁ source, which isevaporated due to the impact of the electron beam. The evaporatedmaterial is then distributed throughout a chamber, and a dielectriclayer of Pr₂O₃ is grown, forming a film on the surface of the structurethat it contacts. The resultant Pr₂O₃ layer includes a thin amorphousinterfacial layer of about 0.5 nm thickness separating a crystallinelayer of Pr₂O₃ from the substrate on which it is grown. This thinamorphous layer is beneficial in reducing the number of interfacecharges and eliminating any grain boundary paths for conductance fromthe substrate. Other source materials can be used for forming the Pr₂O₃layer, as are known to those skilled in the art.

Subsequent to the formation of the Pr₂O₃ layer, another lanthanide oxideis deposited on the film, converting the film from a Pr₂O₃ layer to ananolaminate of Pr₂O₃ and the other lanthanide oxide. In variousembodiments, the other lanthanide oxide is selected from the groupconsisting of Nd₂O₃, Sm₂O₃, Gd₂O₃, and Dy₂O₃. Depending on thelanthanide oxide selected to form the nanolaminate, a correspondingsource material is used in the target for electron beam evaporation. Thesource material for the particular lanthanide oxide is chosen fromcommercial materials for forming the lanthanide oxide by electron beamevaporation, as is known by those skilled in the art.

In one embodiment, alternating layers of Pr₂O₃ and another selectedlanthanide oxide are formed by controlled electron beam evaporationproviding layers of material of predetermined thickness. This controlallows the engineering of a dielectric with a predetermined thicknessand composition. Through evaluation of different lanthanide oxides atvarious thicknesses and number of layers, a dielectric layer with apredetermined t_(eq) in a narrow range of values can be grown.Alternatively, after forming a Pr₂O₃ layer and a layer of anotherlanthanide oxide, additional layers of additional lanthanide oxides canbe formed. Each layer of an additional lanthanide oxide selected from agroup consisting of Pr₂O₃, Nd₂O₃, Sm₂O₃, Gd₂O₃, and Dy₂O₃. Consequently,a dielectric layer can be engineered with electrical characteristicssuited for a given application. These electrical characteristics includet_(eq) and leakage current. A t_(eq) of less than 20 Å can be obtained,typically with sizes of about 14 Å to 8.5 Å.

In an embodiment, nanolaminates of lanthanide oxides are formed byelectron beam evaporation. The lanthanide oxides used in thesenanolaminates are chosen from the group consisting of Pr₂O₃, Nd₂O₃,Sm₂O₃, Gd₂O₃, and Dy₂O₃. The structure of the nanolaminates can bevaried with any one of the group used as the initial layer formed on asubstrate. Typically, the substrate is silicon based, since theselanthanide oxides are thermodynamically stable with respect to formationon a silicon surface. In an alternate embodiment, lanthanide oxidenanolaminates are formed by atomic layer deposition.

A Pr₂O₃ film formed on silicon has a dielectric constant of about 31when formed with little or no interfacial layer between the Pr₂O₃ filmand the substrate. The dielectric constants for the other lanthanideoxides are also in the range of 25-30. As a result, a dielectric layergrown by forming a nanolaminate of lanthanide oxides has a dielectricconstant in the range of about 25 to about 31. However, with aninterfacial layer formed between the surface of the substrate and thefirst lanthanide oxide, the t_(eq) of the dielectric layer is the t_(eq)of the interfacial layer in parallel with the lanthanide oxidenanolaminate. Thus, the dielectric layer formed having an interfaciallayer between the substrate on which it is grown and a lanthanide oxidenanolaminate can have an effective dielectric constant considerably lessthan a dielectric constant associated with a nanolaminate of lanthanideoxides. This is dependent upon the dielectric constant of theinterfacial material being considerably less than the dielectricconstant of the lanthanide oxides used to form the nanolaminate.

A Pr₂O₃ layer can be formed on a silicon based substrate having adielectric constant of about 31 with an interfacial layer of about 0.5nm (5 Å). In another embodiment, for an interfacial layer of about 10.7Å, an effective dielectric constant for a thin layer of Pr₂O₃ on siliconis about 15. Similar effective dielectric constants are associated withthin layers of Nd₂O₃, Sm₂O₃, Gd₂O₃, and Dy₂O₃ oxides on silicon. Forexample, a thin layer of Nd₂O₃ has an effective dielectric constant ofabout 12.9 with an interfacial layer of about 8.2 Å, a thin layer ofSm₂O₃ has an effective dielectric constant of about 11.4 with aninterfacial layer of about 5.5 Å, a thin layer of Gd₂O₃ has an effectivedielectric constant of about 13.9 with an interfacial layer of about 10Å, and a thin layer of Dy₂O₃ has an effective dielectric constant ofabout 14.3 with an interfacial layer of about 12 Å. Lanthanide oxidesgrown on silicon with these reduced effective dielectric constants andcorresponding interfacial layers can be attained with a t_(eq) equal toabout 13 Å for Pr₂O₃, about 12.4 Å for Nd₂O₃, about 12.2 Å for Sm₂O₃,about 13 Å for Gd₂O₃, and about 13.3 Å for Dy₂O₃. Consequently,nanolaminates of these lanthanide oxides can be formed with an effectivedielectric constant in the range of 11 to 15 and a t_(eq) in the rangeof about 12 Å to about 14 Å.

The formation of the interfacial layer is one factor in determining howthin a layer can be grown. An interfacial layer can be SiO₂ for manyprocesses forming a non-SiO₂ dielectric on a silicon substrate. However,advantageously, in an embodiment forming a lanthanide oxide nanolaminatewith an initial layer of Pr₂O₃, a thin amorphous interfacial layer isformed that is not a SiO₂ layer. Typically, this interfacial layer iseither an amorphous layer primarily of Pr₂O₃ formed between the siliconsubstrate and a crystalline form of Pr₂O₃, or a layer of Pr—Si—Osilicate. The dielectric constant for Pr—Si—O silicate is significantlygreater than SiO₂, but not as high as Pr₂O₃.

Another factor setting a lower limit for the scaling of a dielectriclayer is the number of monolayers of the dielectric structure necessaryto develop a full band gap such that good insulation is maintainedbetween an underlying silicon layer and an overlying conductive layer onthe dielectric layer or film. This requirement is necessary to avoidpossible short circuit effects between the underlying silicon layer andthe overlying conductive layer used. In one embodiment, for a 0.5 nminterfacial layer and several monolayers of lanthanide grown, anexpected lower limit for the physical thickness of a dielectric layergrown by forming a lanthanide oxide nanolaminate is anticipated to be inabout the 2-4 nm range. Consequently, typical dielectric layers or filmscan be grown by forming lanthanide oxide nanolaminates having physicalthickness in the range of 4 to 10 nm. The number of layers used, thethickness of each layer, and the lanthanide oxide used for each layercan be engineered to provide the desired electrical characteristics. Theuse of Pr₂O₃ as the initial layer is expected to provide excellentoverall results with respect to reliability, current leakage, andultra-thin t_(eq).

Some embodiments include forming lanthanide oxide nanolaminates byelectron beam evaporation with target material to form Pr₂O₃, forminglanthanide oxide nanolaminates by atomic layer deposition, and electronbeam evaporation forming lanthanide oxide nanolaminates with initiallayers of a lanthanide oxide other than Pr₂O₃. The physical thicknessescan range from about 2 nm to about 10 nm with typical thickness rangingfrom about 4 nm to about 10 nm. Such layers have an effective dielectricconstant ranging from 11 to 31, where a layer with a typical interfaciallayer has an effective dielectric constant in the range of 11 to 16, anda layer with a significantly thin interfacial layer can attain aneffective dielectric constant in the range of 25 to 31. Consequently, arange for the equivalent oxide thickness of a dielectric layer formed asa lanthanide oxide nanolaminate can be engineered over a significantrange. Various embodiments provide a typical t_(eq) of about 14 Å. Withcareful preparation and engineering of the lanthanide oxide nanolaminatelimiting the size of interfacial regions, a t_(eq) down to 2.5 Å orlower is anticipated.

Additional information regarding Pr₂O₃-based La-Oxide dielectric filmscan be found in US Patent Application Publication 20030228747A1,entitled “Pr₂O₃-based La-Oxide Gate Dielectrics,” which is hereinincorporated by reference.

Lanthanide Doped TiO_(x)

A lanthanide doped TiO_(x) dielectric layer can be formed by depositingtitanium and oxygen onto a substrate surface by atomic layer depositionand depositing a lanthanide dopant by atomic layer deposition onto thesubstrate surface containing the deposited titanium and oxygen. Thedopant can be selected from a group consisting of Nd, Tb, and Dy.

In one embodiment, a method of forming a dielectric film includesdepositing titanium and oxygen onto a substrate surface by atomic layerdeposition and depositing a lanthanide dopant by atomic layer depositiononto the substrate surface containing the deposited titanium and oxygen.In one embodiment, the titanium sequence and the lanthanide dopantsequence include using precursors that form oxides of the titanium andthe lanthanide dopant. For example, precursor TiI₄ with H₂O₂ as itsreactant precursor in an ALD process can form TiO_(x), and precursorLa(thd)₃ (thd=2,2,6,6-tetramethyl-3,5-heptanedione) with ozone as itsreactant precursor in an ALD process can form La₂O₃.

Depositing the lanthanide dopant includes regulating the deposition ofthe lanthanide dopant relative to the titanium and oxygen deposited onthe substrate surface to form a dielectric layer containing TiO_(x)doped with a predetermined percentage of the lanthanide. In a furtherembodiment, depositing a lanthanide dopant includes depositing alanthanide selected from a group consisting of Nd, Tb, and Dy.

The lanthanide dopant can be included in the TiO_(x) film usingdifferent embodiments for atomic layer deposition. In one embodiment, alanthanide can be doped in the TiO_(x) film by pulsing a lanthanidedopant sequence in place of a titanium sequence. The lanthanide dopantlevel is then controlled by regulating the number of cycles of thelanthanide dopant sequence with respect to the number of cycles of thetitanium sequence. In another embodiment, a lanthanide can be doped inthe TiO_(x) film by pulsing a lanthanide dopant precursor substantiallysimultaneously with a titanium precursor. The titanium/lanthanide dopantsequence includes a precursor for oxidizing the titanium/lanthanidedopant at the substrate surface. The lanthanide dopant level is thencontrolled by regulating the mixture of the titanium-containingprecursor and the lanthanide-containing precursor.

Dielectric films of lanthanide doped TiO_(x) formed by atomic layerdeposition can provide not only ultra thin t_(eq) films, but also filmswith relatively low leakage current. In addition to using ALD to provideprecisely engineered film thicknesses, attainment of relatively lowleakage current is engineered by doping with lanthanides selected from agroup consisting of Nd, Tb, and Dy. Though a layer of undoped TiO_(x)can be amorphous, which assists the reduction of leakage current, dopingwith these lanthanides yields a doped amorphous TiO_(x) with enhancedleakage current characteristics. Leakage currents on the order of 10⁻⁷A/cm² or smaller in TiO_(x) layers doped with Nd, Tb, or Dy can beattained, which are orders of magnitude smaller than for undopedTiO_(x). Further, the breakdown electric fields are several factorslarger for layers of TiO_(x) doped with Nd, Tb, or Dy than for layers ofundoped TiO_(x).

The doping of the TiO_(x) layer with a lanthanide occurs as asubstitution of a lanthanide atom for a Ti atom. The resultant dopedTiO_(x) layer is a layer of amorphous Ti_(1-y)L_(y)O_(x), where L is alanthanide. Controlling the ALD cycles of the titanium sequence and thelanthanide dopant sequence allows a Ti_(1-y)L_(y)O_(x), or lanthanidedoped TiO_(x), dielectric layer to be formed where the lanthanide, L,can range from about 5% to about 40% of the dielectric layer formed.Such TiO_(x) layers doped with Nd, Tb, or Dy formed by ALD can providethe reduced leakage current and increased breakdown mentioned above.

Additional information regarding lanthanide doped TiO_(x) dielectricfilms can be found in US Patent Application Publication 2004/0043541A1,entitled “Atomic Layer Deposited Lanthanide Doped TiOx DielectricFilms,” which is herein incorporated by reference.

HfSiON

A HfSiON dielectric can be formed by atomic layer deposition. A HfSiONlayer thickness is controlled by repeating for a number of cycles asequence including pulsing a hafnium-containing precursor into areaction chamber, pulsing an oxygen-containing precursor into thereaction chamber, pulsing a silicon-containing precursor into thereaction chamber, and pulsing a nitrogen-containing precursor until adesired thickness is formed.

The hafnium-containing precursor includes a HfCl₄ precursor in someembodiments, and a HfI₄ precursor in other embodiments. According tosome embodiments, the oxygen-containing precursor includes water vaporor a vapor solution of H₂O—H₂O₂ into the reaction chamber. According tosome embodiments, the silicon-containing precursor includes a SiCl₄precursor. A nitrogen-containing precursor includes a NH₃ precursor insome embodiments. NH₃ annealing at about 550° C. can also be performed.

Additional information regarding HfSiON dielectric films can be found inUS Patent Application Publication 2004/0043569A1, entitled “Atomic LayerDeposited HfSiON Dielectric Films,” which is herein incorporated byreference.

Zr—Sn—Ti—O

A Zr—Sn—Ti—O dielectric layer can be formed by depositing titanium andoxygen onto a substrate surface by atomic layer deposition, depositingzirconium and oxygen onto a substrate surface by atomic layerdeposition, and depositing tin and oxygen onto a substrate surface byatomic layer deposition. Metal chloride precursors can be pulsed foreach metal in the Zr—Sn—Ti—O. In some embodiments, the dielectric filmis formed by forming TiO₂ onto a surface by atomic layer deposition,depositing zirconium and oxygen onto the surface by atomic layerdeposition, and depositing tin and oxygen onto the surface by atomiclayer deposition. The TiO₂ deposition can include pulsing a TiCl₄precursor. The zirconium and oxygen deposition can include pulsing aZrCl₄ precursor. The tin and oxygen deposition can include pulsing aSnCl₄ precursor. In various embodiments, the formation of the dielectricfilm is controlled such that the dielectric film has a compositionsubstantially of Zr_(y)Sn_(x)Ti_(1-x-y)O₄ with 0.3<y<0.7 and 0<x<0.2.

In some embodiments, the dielectric film is formed by forming TiO₂ ontoa surface by atomic layer deposition using a TiI₄ precursor; depositingzirconium and oxygen by atomic layer deposition using a zirconium halideprecursor following forming TiO₂; and depositing tin and oxygen byatomic layer deposition using a tin halide precursor followingdepositing zirconium and oxygen. The zirconium and oxygen deposition caninclude pulsing a ZrI₄ precursor. The tin and oxygen deposition caninclude pulsing a SnI₄ precursor. In various embodiments, the formationof the dielectric film is controlled such that the dielectric film has acomposition substantially of Zr_(y)Sn_(x)Ti_(1-x-y)O₄ with 0.3<y<0.7 and0<x<0.2. In various embodiments, the formation of the dielectric film iscontrolled such that the dielectric film has a composition substantiallyof Zr_(0.2)Sn_(0.2)Ti_(0.6)O₂.

Additional information regarding Zr—Sn—Ti—O dielectric films can befound in US Patent Application Publication 2004/0110391A1, entitled“Atomic Layer Deposited Zr—Sn—Ti—O Films,” and US Patent ApplicationPublication 2004/0110348A1, entitled “Atomic Layer Deposited Zr—Sn—Ti—OFilms using TiI₄,” which are herein incorporated by reference.

Metal Oxynitride

The high-k dielectric film can be formed as a metal oxynitride, formedby atomic layer deposition of a plurality of reacted monolayers. Themonolayers comprise at least one each of a metal, an oxide and anitride. According to various embodiments, the metal oxynitride layer isformed from zirconium oxynitride, hafnium oxynitride, tantalumoxynitride, or mixtures thereof.

According to various process embodiments, a plurality of gaseousprecursors can be separately introduced to a surface of thesemiconductor substrate. The gaseous precursors comprise a metal gaseousprecursor and at least two nonmetallic gaseous precursors. A firstgaseous precursor of the plurality of gaseous precursors is purged orevacuated from the surface of the semiconductor substrate before asecond gaseous precursor of the plurality of gaseous precursors isintroduced to the surface of the semiconductor substrate. The metalgaseous precursor can include zirconium tetrachloride, zirconiumtetraiodide, hafnium tetrachloride, hafnium tetraiodide, or ahalogenated tantalum. An oxygen-containing gaseous precursor and anitrogen-containing gaseous precursor are separately introduced to thesurface of the semiconductor substrate. For example, water or hydrogenperoxide can be used as the oxygen-containing gaseous precursor and atleast one of ammonia, tert-butylamine, allylamine, and1,1-dimethylhydrazine can be used as the nitrogen-containing gaseousprecursor. Thus, monolayers of metal, oxide, and nitride are formed, andthe metal, oxide, and nitride monolayers are reacted to form the metaloxynitride layer.

Additional information regarding metal oxynitride dielectric layers canbe found in US Patent Application Publication 2004/0144980A 1, entitled“Atomic Layer Deposition of Metal Oxynitride Layers as Gate Dielectricsand Semiconductor Device Structures Utilizing Metal Oxynitride Layers,”which is herein incorporated by reference.

HfO₂/Hf

The high-k dielectric film can be HfO₂/Hf, which can be formed bydepositing a hafnium metal layer on a substrate surface by atomic layerdeposition and depositing a hafnium oxide layer on the hafnium metallayer by atomic layer deposition to form a hafnium oxide dielectriclayer substantially free of silicon oxide. In general, a layer of ametal is formed on a substrate by atomic layer deposition, and an oxideof the metal is formed on the metal by atomic layer deposition.

A hafnium nitrate precursor, such as an anhydrous hafnium nitrateprecursor, can be used to form the layer of hafnium. A layer of hafniumoxide can be formed using an anhydrous hafnium nitrate precursor and awater vapor precursor. The substrate may be maintained at about 180° C.during the formation of the layer of hafnium and the formation of thelayer of hafnium oxide.

Additional information regarding metal oxide/metal dielectric films,such as HfO₂/Hf, can be found in US Patent Application Publication2004/0175882A1, entitled “Atomic Layer Deposited Dielectric Layers,”which is herein incorporated by reference.

ZrAl_(x)O_(y)

The high-k dielectric film can be ZrAl_(x)O_(y), which can be formed byALD by pulsing a zirconium-containing precursor onto a substrate,pulsing a first oxygen-containing precursor, pulsing analuminum-containing precursor, and pulsing a second oxygen-containingprecursor to form ZrAl_(x)O_(y). A precursor can be used that includesboth zirconium and oxygen to provide the zirconium and oxygen in onepulsing process, and a precursor can be used that contains both aluminumand oxygen to provide the aluminum and oxygen in one pulse. In variousembodiments, the dielectric layer contains Zr₄AlO₉. An interfacial layerof silicon oxide or silicon between the substrate and the ZrAl_(x)O_(y)dielectric can be less than about 1 nm. The zirconium-containingprecursor can be selected from ZrCl₄ and ZrI₄ precursors. Thealuminum-containing precursor can be selected from trimethylaluminum andDMEAA. Oxygen-containing precursors can be selected from H₂O, H₂O₂, anda H₂O—H₂O₂ mixture.

Additional information regarding ZrAl_(x)O_(y) dielectric layers can befound in US Patent Application Publication 2005/0054165A1, entitled“Atomic Layer Deposited ZrAl_(x)O_(y) Dielectric Layers,” which isherein incorporated by reference.

ZrTiO₄

The high-k dielectric film can be ZrTiO₄, which can be formed by ALD bypulsing a titanium-containing precursor onto a substrate, and pulsing azirconium-containing precursor to form an oxide containing Zr and Ti.The pulsing of the titanium-containing precursor and the pulsing of thezirconium-containing precursor is controlled to provide a dielectriclayer with a predetermined zirconium to titanium ratio. In variousembodiments, the ZrTiO₄ film is formed with a Zr/Ti ratio of about0.4/0.6. A zirconium-containing precursor used to form the oxidecontaining Zr and Ti can include zirconium tertiary-butoxide. Thetitanium-containing precursor can be selected from TiCl₄, TiI₄,Ti(OCH(CH₃)₂)₄, and Ti(OC₂H₅)₄. The first pulsing of thetitanium-containing precursor can be performed before pulsing thezirconium tertiary-butoxide precursor.

Reactant precursors that can be used after pulsing thetitanium-containing precursor and pulsing the zirconiumtertiary-butoxide precursor can be selected from H₂O, H₂O₂, ROH, N₂O,O₃, and O₂. The substrate can be kept at a temperature ranging fromabout 200° C. to about 400° C. A silicon nitride layer can be formedbetween the substrate and the film containing ZrTiO₄. The ALD-formedfilm can be a nanolaminate of ZrO₂ and TiO₂.

Additional information regarding ZrTiO₄ dielectric layers can be foundin US Patent Application Publication 2004/0214399A1, entitled “AtomicLayer Deposited ZrTiO₄ Films,” which is herein incorporated byreference.

Zr-Doped Ta Oxide

The high-k dielectric film can be a zirconium-doped tantalum oxidedielectric layer, such as can be formed by depositing tantalum by atomiclayer deposition onto a substrate surface and depositing a zirconiumdopant by atomic layer deposition onto the substrate surface. Theformation of the zirconium-doped tantalum oxide can include pulsing atantalum-containing precursor to deposit tantalum onto a substratesurface, pulsing an oxygen-containing precursor to deposit oxygen ontothe substrate surface, repeating for a number of cycles the pulsing ofthe tantalum-containing precursor and the pulsing of theoxygen-containing precursor, and substituting a zirconium cycle for oneor more cycles of the pulsing of the tantalum-containing precursor. Thezirconium cycle includes pulsing a zirconium-containing precursor todeposit zirconium onto the substrate surface. A reactant precursor isselected to produce an oxidizing reaction for the zirconium at thesubstrate surface. According to various embodiments, atantalum-containing precursor includes Ta(OC₂H₅)₅, and azirconium-containing precursor includes ZrI₄.

Additional information regarding zirconium-doped tantalum oxidedielectric layers can be found in U.S. patent application Ser. No.10/909,959, filed Aug. 2, 2004, entitled “Atomic Layer Deposition ofZirconium-Doped Tantalum Oxide Films,” which is herein incorporated byreference.

HfO₂—Si₃N₄ on SiO₂

The high-k dielectric layer can be formed by depositingHfO₂-Silicon-Nitride by atomic layer deposition. TheHfO₂-Silicon-Nitride is formed on SiO₂. The silicon nitride can beformed using SiCl₄ and NH₃ gases, and HfO₂ can be formed by ALD usinghafnium tetraiodide and oxygen as precursors. Anhydrous Hf(NO₃)₄ and H₂Ovapor may also be used.

Ru Gate and La-Oxide

Various embodiments use a lanthanide oxide high-k dielectric with aruthenium or ruthenium oxide gate. In various embodiments, thelanthanide oxide dielectric layer is formed by depositing lanthanum byatomic layer deposition onto a substrate surface using atrisethylcyclopentadionatolanthanum precursor or atrisdipyvaloylmethanatolanthanum precursor. A ruthenium gate on alanthanide oxide dielectric layer provides a gate structure thateffectively prevents a reaction between the gate and the lanthanideoxide dielectric layer.

Additional information regarding ruthenium on lanthanide oxide can befound in U.S. patent application Ser. No. 10/926,812, filed Aug. 26,2004, entitled “Ruthenium Gate For a Lanthanide Oxide Dielectric Layer,”which is herein incorporated by reference.

TiAlO_(X)

The high-k dielectric film can be provided by a titanium aluminum oxidefilm, which can be formed by depositing titanium and/or aluminum byatomic layer deposition onto a substrate surface. The deposited titaniumand/or aluminum is annealed using atomic oxygen. After annealing, alayer of titanium aluminum oxide is formed on the annealed layer to forma contiguous layer of titanium aluminum oxide.

Forming the dielectric includes forming an insulating metal oxide, whichincludes forming a first layer of at least one of a first metal and asecond metal by atomic layer deposition, annealing the first layer usingoxygen, and forming, after annealing the first layer, a second layer ofan insulating metal oxide of the first metal and the second metal ontothe first layer by atomic layer deposition to form a contiguous layer.The first layer can include a layer of the first metal and the secondmetal. The first layer can have a thickness of about one monolayer or atmost substantially two monolayers.

According to various embodiments, a first layer of titanium aluminumoxide is formed by atomic layer deposition, and the first layer isannealed using atomic oxygen. A second layer of titanium aluminum oxideis formed onto the first layer by atomic layer deposition, afterannealing the first layer, to form a contiguous layer. The first layerof titanium aluminum oxide can be formed using TiI₄ or trimethylaluminumas a precursor, and the second layer of titanium aluminum oxide can beformed using TiCl₄ as a precursor. The titanium oxide and the titaniumaluminum oxide film can be formed as a nanolaminate.

Additional information regarding titanium aluminum oxide films can befound in U.S. patent application Ser. No. 10/931,533, filed Aug. 31,2004, entitled “Atomic Layer Deposited Titanium Aluminum Oxide Films,”which is herein incorporated by reference.

LaAlO_(X)

The high-k dielectric film can be provided by a lanthanum aluminum oxidedielectric layer, which can be formed by depositing aluminum andlanthanum by atomic layer deposition onto a substrate surface in whichprecursors to deposit the lanthanum include atrisethylcyclopentadionatolanthanum precursor and/or atrisdipyvaloylmethanatolanthanum precursor, and a metal (e.g. Al)containing precursor is also used. The lanthanum aluminum oxide can beformed as a compound of lanthanum oxide and aluminum oxide. Thedielectric layer can include LaAlO₃.

Additional information regarding titanium aluminum oxide films can befound in U.S. patent application Ser. No. 10/930,167, filed Aug. 31,2004, entitled “Atomic Layer Deposited Lanthanum Aluminum OxideDielectric Layer,” which is herein incorporated by reference.

La₂Hf₂O₇

The high-k dielectric can be provided as a lanthanum hafnium oxidelayer, which can be formed by depositing hafnium and lanthanum by atomiclayer deposition onto a substrate surface. The process includesintroducing a lanthanum-containing precursor to a substrate, andintroducing a hafnium-containing precursor to the substrate. Embodimentsinclude methods and apparatus in which precursors to deposit thelanthanum include a trisethylcyclopentadionatolanthanum (La(EtCp)₃)precursor, a tris(2,2,6,6-tetramethyl-3,5-heptanedionato)lanthanum (III)precursor, a trisdipyvaloylmethanatolanthanum precursor, or atris(2,2,6,6-tetramethyl-3,5-heptanedionato)lanthanum (III) tetraglymeadduct precursor.

Additional information regarding titanium aluminum oxide films can befound in U.S. patent application Ser. No. 11/010,529, filed Dec. 13,2004, entitled “Atomic Layer Deposited Lanthanum Hafnium OxideDielectrics,” which is herein incorporated by reference.

HfTaO

The high-k dielectric can be provided as a hafnium tantalum oxide film,which can be formed by depositing hafnium and tantalum by atomic layerdeposition onto a substrate surface. A tantalum-containing precursor caninclude a tantalum ethoxide precursor, and a hafnium-containingprecursor can include a hafnium nitrate precursor.

Additional information regarding titanium aluminum oxide films can befound in U.S. patent application Ser. No. 11/029,757, filed Jan. 5,2005, entitled “Atomic Layer Deposited Hafnium Tantalum OxideDielectrics,” which is herein incorporated by reference.

Hafnium Titanium Oxide

The high-k dielectric can be provided as hafnium titanium oxide, such asHfTiO₄, formed by ALD using precursors substantially free of chlorineand carbon. Precursors capable of being used include a titanium halideprecursor such as a titanium iodine precursor, a titanium nitrideprecursor, a titanium isopropoxide precursor, and a hafnium halideprecursor such as a hafnium chloride precursor.

Amorphous Lanthanide Doped TiO_(X)

The high-k dielectric can be provided as an ALD-formed amorphousdielectric layer of titanium oxide (TiO_(X)) doped with lanthanideelements, such as samarium, europium, gadolinium, holmium, erbium andthulium. The dielectric structure is formed by depositing titanium oxideby atomic layer deposition onto a substrate surface using precursorchemicals, followed by depositing a layer of a lanthanide dopant, andrepeating to form a sequentially deposited interleaved structure. Theleakage current of the dielectric layer is reduced when the percentageof the lanthanide element doping is optimized. The amorphous dielectriclayer is formed on a substrate by atomic layer deposition at apredetermined temperature, such as within a range of approximately 100°C. to 250° C. The amorphous dielectric layer can be comprised of aplurality of individual titanium oxide layers, with at least onelanthanide layer interleaved between each individual one of the titaniumoxide layers. The dielectric layer can have a titanium to lanthanideratio selected to obtain a dielectric constant value of from 50 to 100,and can be selected with a titanium to lanthanide ratio selected toobtain a leakage current of less than 10⁻⁸ A/cm² and a breakdown voltageof greater than 2.0 MV/cm.

Additional information regarding titanium aluminum oxide films can befound in U.S. patent application Ser. No. 11/092,072, filed Mar. 29,2005, entitled “ALD of Amorphous Lanthanide Doped TiO_(X) Films,” whichis herein incorporated by reference.

Ti Gate Dielectric

The high-k dielectric can be provided as a Ti gate dielectric, which maybe formed by providing a substrate assembly in a vacuum chamber, andforming a gate dielectric on the surface, including forming a metaloxide on at least a portion of the surface of the substrate assembly byelectron beam evaporation, and generating an ion beam using an inert gasto provide inert gas ions for contacting the metal oxide duringformation thereof. An environment including oxygen (e.g. ozone) can beprovided in the vacuum chamber to form the metal oxide in the oxygenenvironment. The metal oxide can be selected from the group consistingof TiO₂, Y₂O₃, Al₂O₃, ZrO₂, HfO₂, Y₂O₃—ZrO₂, ZrSiO₄, LaAlO₃, andMgAl₂O₄.

Additional information regarding-titanium aluminum oxide films can befound in U.S. Pat. No. 6,495,436, entitled “Formation Of Metal OxideGate Dielectric,” which is herein incorporated by reference.

TiO₂

The high-k dielectric can be provided as a TiO₂ dielectric, which can bephysically vapor formed as a high purity metal layer over thesemiconductor substrate. After forming such a layer, the high puritymetal layer can be oxidized employing atomic oxygen generated in a highdensity plasma environment to form the dielectric material. Thephysically vapor formed high purity metal layer can have at least about99.9% purity over the semiconductor substrate. The physical vaporformation can include electron beam evaporation. Prior to the electronbeam evaporation, the vacuum chamber can be evacuated to a base pressureof about 1×10⁻⁷ Torr or lower, and a low-energy ion-bombardment sourceis directed towards the semiconductor substrate during the electron beamevaporation. A low-energy argon ion-bombardment can be directed towardsthe semiconductor substrate during the electron beam evaporation. Thehigh purity metal layer can include two or more high purity metals, suchas a metal-silicon alloy. The high purity metal can be selected fromtitanium, yttrium, zirconium, hafnium and various mixtures thereof.

Additional information regarding TiO₂ films can be found in U.S. Pat.No. 6,534,420, entitled “Methods For Forming Dielectric Materials andMethods for Forming Semiconductor Devices,” which is herein incorporatedby reference.

Amorphous HfO₂

The high-k dielectric can include hafnium oxide, which can be formed byforming a thin hafnium (Hf) film by thermal evaporation at a lowsubstrate temperature, and radically oxidizing the thin hafnium filmusing a krypton/oxygen (Kr/O₂) high-density plasma to form the gatedielectric layer of hafnium oxide (HfO₂). The resulting gate dielectriclayer is thermally stable in contact with silicon and is resistive toimpurity diffusion at the HfO₂/silicon interface. The formation of theHfO₂ eliminates the need for a diffusion barrier layer, allows thicknessuniformity of the field oxide on the isolation regions, and preservesthe atomically smooth surface of the silicon substrate. The hafniumlayer can be formed by electron beam evaporation.

Additional information regarding HfO₂ and other amorphous high-k gateoxide films can be found in U.S. Pat. No. 6,514,828, entitled “Method ofFabricating a Highly Reliable Gate Oxide,” which is herein incorporatedby reference.

CrTiO₃

The high-k dielectric can be provided by CrTiO₃, which can be formedfrom alloys such as cobalt-titanium. These alloys are thermodynamicallystable such that the gate dielectrics formed will have minimal reactionswith a silicon substrate or other structures during any later hightemperature processing stages. The underlying substrate surfacesmoothness is preserved by using a thermal evaporation technique todeposit the layer to be oxidized. A metal alloy layer is evaporationdeposited on the body region, and the metal alloy layer is oxidized toform a metal oxide layer on the body region. Cobalt and titanium can beevaporation deposited, such as by electron beam evaporation. Theevaporation deposition of the metal alloy layer can be performed at asubstrate temperature range of 100-150° C., and the oxidation of themetal alloy layer can be performed at a temperature of approximately400° C. A krypton (Kr)/oxygen (O₂) mixed plasma can be used in theoxidization process.

Additional information regarding HfO₂ and other amorphous high-k gateoxide films can be found in US Patent Publication No. 2003/0119246A1,entitled “Low-Temperature Grown High Quality Ultra-Thin CoTiO₃ GateDielectrics,” which is herein incorporated by reference.

Oxides of Group IVB Elements (e.g. ZrO₂)

The high-k gate dielectric can be formed from elements like zirconium,such as ZrO₂, which are thermodynamically stable such that the gatedielectric will have little reaction with a silicon substrate or otherstructures during any later high temperature processing stages. The gatedielectric can be formed by evaporation depositing a metal layer on thebody region, the metal being chosen from the group IVB elements of theperiodic table, and oxidizing the metal layer to form a metal oxidelayer on the body region. The metal layer can include a zirconium layer,which can be deposited by electron beam evaporation. The substratetemperature range for the deposition can be within a range of 150-400°C. The oxidation can be performed using atomic oxygen or with a krypton(Kr)/oxygen (O₂) mixed plasma, for example.

Additional information regarding ZrO₂ and other amorphous high-k gateoxide films can be found in US Patent Publication No. 2003/0045078A1,entitled “Highly Reliable Amorphous High-K Gate Oxide ZrO₂,” which isherein incorporated by reference.

Group IIIB/Rare Earth Series (Crystalline or Amorphous Y₂O₃ and Gd₂O₃)

The high-k dielectric can be provided using elements such as yttrium andgadolinium, which are thermodynamically stable such that the resultinggate dielectrics have minimal reaction with a silicon substrate or otherstructures during any later high temperature processing stages. Theunderlying substrate surface smoothness is preserved using a thermalevaporation technique to deposit the layer to be oxidized. The gatedielectric can be formed by evaporation depositing a metal layer on thebody region, where the metal is chosen from a group consisting of thegroup IIIB elements and the rare earth series of the periodic table, andby oxidizing the metal layer to form a metal oxide layer on the bodyregion. The metal layer can be yttrium and can be gadolinium. Electronbeam evaporation can be used. The substrate temperature for thedeposition can be approximately 150-400° C. Atomic oxygen and a krypton(Kr)/oxygen (O₂) mixed plasma can be used to oxidize the metal layer,for example.

Additional information regarding gate oxides formed from elements suchas yttrium and gadolinium can be found in U.S. Pat. No. 6,844,203entitled “Gate Oxides, and Methods of Forming,” which is hereinincorporated by reference.

Praseodymium Oxide

The gate dielectric can be provided by a praseodymium oxide. The Pr gateoxide is thermodynamically stable so that the oxide reacts minimallywith a silicon substrate or other structures during any later hightemperature processing stages. The underlying substrate surfacesmoothness is preserved using a thermal evaporation technique to deposita Pr layer to be oxidized. The gate dielectric can be formed byevaporation depositing a praseodymium (Pr) layer on the body region, andoxidizing the Pr layer to form a Pr₂O₃ layer on the body region.Electron beam evaporation can be used. The substrate temperature for thedeposition can be in an approximate range of 150-400° C. Atomic oxygenand a krypton (Kr)/oxygen (O₂) mixed plasma can be used to oxidize thePr layer, for example. The Pr₂O₃ layer can be formed to have anequivalent oxide thickness of less than 2 nm.

Additional information regarding praseodymium gate oxides can be foundin U.S. Pat. No. 6,900,122, entitled “Low-Temperature Grown High-QualityUltra-Thin Praseodymium Gate Dielectrics,” which is herein incorporatedby reference.

ZrO_(X)N_(Y)

The high-k dielectric can be provided by a metal oxynitride such asZrO_(X)N_(Y). The addition of nitrogen to the microstructure of the gatedielectric promotes an amorphous phase that provides the gate dielectricwith improved electrical properties. The underlying substrate surfacesmoothness is preserved by using a thermal evaporation technique tofirst deposit a metal layer. The gate dielectric can be formed byevaporation depositing a metal layer such as a zirconium layer on thebody region, oxidizing the metal layer, and nitriding the metal layer.Electron beam evaporation can be used. The substrate temperature for thedeposition can be in an approximate temperature range of 150-400° C.Atomic oxygen and a krypton (Kr)/oxygen (O₂) mixed plasma, for example,can be used to oxidize the metal layer. The metal layer can be annealedin NH₃ at a temperature of approximately 700° C.

Additional information regarding ZrO_(X)N_(Y) gate oxides can be foundin U.S. Pat. No. 6,767,795 entitled “Highly Reliable Amorphous High-KGate Dielectric ZrO_(X)N_(Y),” which is herein incorporated byreference.

LaAlO₃

The high-k dielectric can be provided by LaAlO₃. A LaAlO₃ gatedielectric can be formed by evaporating Al₂O₃ at a given rate,evaporating La₂O₃ at another rate, and controlling the two rates toprovide an amorphous film containing LaAlO₃ on a transistor body region.The evaporation deposition of the LaAlO₃ film is performed using twoelectron guns to evaporate dry pellets of Al₂O₃ and La₂O₃. The two ratesfor evaporating the materials are selectively chosen to provide adielectric film composition having a predetermined dielectric constantranging from the dielectric constant of an Al₂O₃ film to the dielectricconstant of a La₂O₃ film. Electron beam evaporation can be used. Apredetermined dielectric constant can be achieved by controlling theevaporation rates.

Additional information regarding evaporated LaAlO₃ gate dielectrics canbe found in U.S. Pat. No. 6,893,984, entitled “Evaporated LaAlO₃ Filmsfor Gate Dielectrics,” which is herein incorporated by reference.

TiO_(X)

The high-k dielectric can be provided by TiO_(X). The dielectric filmcan be formed by ion assisted electron beam evaporation of TiO₂ andelectron beam evaporation of a lanthanide selected from a groupconsisting of Nd, Tb, and Dy. The growth rate is controlled to provide adielectric film having a lanthanide content ranging from about ten toabout thirty percent of the dielectric film. These dielectric filmscontaining lanthanide doped TiO_(x) are amorphous and thermodynamicallystable such that the lanthanide doped TiO_(x) will have minimal reactionwith a silicon substrate or other structures during processing.

The film can be formed by evaporating TiO₂ at a first rate, evaporatinga lanthanide at a second rate, and controlling the first rate and thesecond rate to grow a dielectric film on a substrate, the dielectricfilm containing TiO_(x) doped with the lanthanide. The lanthanide can beselected from a group consisting of Nd, Tb, Dy. Electron beamevaporation can be used. The rates can be controlled to selectively growthe dielectric film doped in the range from about 10% to about 30%lanthanide. The rates can be controlled so that the dielectric film hasa dielectric constant ranging from about 50 to about 110.

Additional information regarding evaporated lanthanide doped TiO_(X)dielectric films can be found in U.S. Pat. No. 6,790,791 entitled“Lanthanide Doped TiOx Dielectric Films,” which is herein incorporatedby reference.

TiO_(X) by Kr Plasma Oxidation

The high-k dielectric can be provided by TiO_(X), which can be formed byion assisted electron beam evaporation of Ti, electron beam evaporationof a lanthanide selected from a group consisting of Nd, Tb, and Dy, andoxidation of the evaporated Ti/lanthanide film in a Kr/oxygen plasma.The growth rate is controlled to provide a dielectric film having alanthanide content ranging from about five to about forty percent of thedielectric film. These dielectric films containing lanthanide dopedTiO_(x) are amorphous and thermodynamically stable such that thelanthanide doped TiO_(x) will have minimal reaction with a siliconsubstrate or other structures during processing. Electron beamevaporation can be used. The rates can be controlled to provide alanthanide doped Ti film on the substrate for growing a dielectric filmdoped in the range from about 5% to about 40% lanthanide. The rates canbe controlled to provide the film with a dielectric constant rangingfrom about 50 to about 110.

Additional information regarding evaporated lanthanide doped TiO_(X)dielectric films can be found in U.S. Pat. No. 6,884,739 entitled“Lanthanide Doped TiO_(X) Dielectric Films By Plasma Oxidation,” whichis herein incorporated by reference.

Y—Si—O

The dielectric can be provided by Y—Si—O dielectrics formed byevaporation deposition techniques.

Oxidation of Metals

The high-k dielectric can be provided by oxidizing metal. Examples ofmetal oxides include PbO, Al₂O₃, Ta₂O₅, TiO₂, ZrO₂, and Nb₂O₅.

Additional information regarding oxidation of metals for high-kdielectrics can be found in US Patent Application Publication2003/0043637 entitled “Flash Memory With Low Tunnel Barrier InterpolyInsulators,” which is herein incorporated by reference.

HfO₂/La₂O₃

The high-k dielectric can be provided by an HfO₂/La₂O₃ nanolaminatestructure. The dielectric can be formed by forming a firstmetal-containing dielectric layer over the surface of the substrate, themetal comprising an element selected from Group IVB of the periodictable, and forming a second metal-containing dielectric layer over thefirst metal-containing dielectric layer. For example, the firstmetal-containing dielectric layer can include hafnium, and the secondmetal-containing dielectric layer comprises lanthanum.

A layer of silicon dioxide can be formed to overlie at least one portionof the surface; and the first metal-containing dielectric layer can beformed by forming a metal layer over the layer of silicon dioxide, andcombining metal of the metal layer with oxygen of the silicon dioxidelayer to form a metal oxide dielectric material. The secondmetal-containing dielectric layer can be an element selected from GroupIIIB of the periodic table.

According to various embodiments, the dielectric is formed by forming ahafnium-containing layer, forming a lanthanum-containing layer over thehafnium-containing layer, and exposing the hafnium-containing layer andthe lanthanum-containing layer to an oxygen-comprising atmosphere andheating the hafnium-containing layer and the lanthanum-containing layerto a temperature effective to form a hafnium-containing dielectric layerand a lanthanum-containing dielectric layer. Physical vapor depositioncan be used. The thickness of each of the hafnium-containing dielectriclayer and the lanthanum-containing dielectric layer can be less thanabout 5 nm. The ratio of the hafnium thickness to the lanthanumthickness can be from about 1 to 3 to about 1 to 4.

Additional information regarding nanolaminates such as HfO₂/La₂O₃ ashigh-k dielectrics can be found in US Patent Application Publication2002/0192974 entitled “Dielectric Layer Forming Method and DevicesFormed Therewith,” which is herein incorporated by reference.

La₂O₃/Hf₂O₃

The high-k dielectric can be provided by an La₂O₃/Hf₂O₃ nanolaminate.Alternate layers of hafnium oxide and lanthanum oxide over a substratecan be deposited to form a composite. The dielectric can be provided byforming one hafnium oxide monolayer, forming one lanthanum oxidemonolayer, and repeating to form a plurality of single hafnium oxidemonolayers interspersed among a plurality of single lanthanum oxidemonolayers. Multiple hafnium oxide monolayers can be formed to create ahafnium oxide multilayer, and multiple lanthanum oxide monolayers can beformed to create a lanthanum oxide multilayer. A plurality of hafniumoxide multilayers can be interspersed among a plurality of lanthanumoxide multilayers. The hafnium oxide can comprise thermally stable,crystalline hafnium oxide, and the lanthanum oxide can comprisethermally stable, crystalline lanthanum oxide.

According to various methods, at least one monolayer of a first materialis chemisorbed over a substrate, where the first material comprises afirst metal. At least some of the chemisorbed first material is treatedand an oxide of the first metal is formed. At least one monolayer of asecond material (second metal) is chemisorbed on the first metal-oxide.An oxide of the second metal is formed. One of the first and secondmetals comprises hafnium and the other comprises lanthanum. The firstmaterial can comprise HfCl₄, and the chemisorbed first material can betreated by exposure to H₂O to form HfO₂. The first material can compriseLa(thd)₃, and the chemisorbed first material can be treated by exposureto H₂O to form La₂O₃.

Additional information regarding nanolaminates such a La₂O₃/Hf₂O₃ ashigh-k dielectrics can be found in US Patent Application Publication2004/0038554 entitled “Composite Dielectric Forming Methods andComposite Dielectrics,” which is herein incorporated by reference.

HfO₂/ZrO₂

The high-k dielectric can be provided by a HfO₂/ZrO₂ nanolaminate, whichcan be formed by atomic layer deposition of HfO₂ using a HfI₄ precursorfollowed by the formation of ZrO₂ on the HfO₂ layer. The HfO₂ layerthickness is controlled by repeating for a number of cycles a sequenceincluding pulsing the HfI₄ precursor into a reaction chamber, pulsing apurging gas into the reaction chamber, pulsing a first oxygen-containingprecursor into the reaction chamber, and pulsing the purging gas untilthe desired thickness is formed. These gate dielectrics containingHfO₂/ZrO₂ nanolaminates are thermodynamically stable such that theHfO₂/ZrO₂ nanolaminates will have minimal reaction with a siliconsubstrate or other structures during processing.

The layer of zirconium oxide can be formed by rapid thermal CVD at about500° C. A nitrogen anneal between about 700° C. and about 900° C. can beperformed after the layer of zirconium oxide is formed. The layer ofhafnium oxide can be formed by pulsing a first oxygen-containingprecursor, such as water vapor, into the reaction chamber after pulsingthe HfI₄ precursor into the reaction chamber.

Additional information regarding nanolaminates such a HfO₂/ZrO₂ ashigh-k dielectrics can be found in US Patent Application Publication2004/0023461 entitled “Atomic Layer Deposited Nanolaminates of HfO₂/ZrO₂films as Gate Dielectrics,” which is herein incorporated by reference.

Lanthanide Oxide/Zirconium Oxide

The high-k dielectric can be provided by a lanthanide oxide/zirconiumoxide nanolaminate. According to various embodiments, the ZrO₂ isdeposited by multiple cycles of reaction sequence atomic layerdeposition (RS-ALD) that includes depositing a ZrI₄ precursor onto thesurface of the substrate in a first pulse followed by exposure toH₂O/H₂O₂ in a second pulse, thereby forming a thin ZrO₂ layer on thesurface. After depositing the ZrO₂ layer, the lanthanide oxide layer isdeposited by electron beam evaporation. The composite laminate zirconiumoxide/lanthanide oxide dielectric layer has a relatively high dielectricconstant and can be formed in layers of nanometer dimensions.

Various embodiments provide a layer of ZrO₂, and a layer of a lanthanideoxide having a thickness of about 2-12 nm on the ZrO₂ layer. The ZrO₂layer has a thickness of about 1-6 nm, and the composite laminatedielectric layer has a thickness of about 3-18 nm. The lanthanide oxidecan include Pr₂O₃, Nd₂O₃, Sm₂O₃, Gd₂O₃, Dy₂O₃ and PrTi_(X)O_(Y).According to various embodiments, the composite laminate dielectriclayer has a dielectric constant between about 12 and about 23. The ZrO₂layer can be formed by atomic layer deposition from a ZrI₄ precursorfollowed by oxidation with H₂O/H₂O₂, and the lanthanide oxide layer canbe formed by electron beam evaporation of a lanthanide oxide.

Additional information regarding nanolaminates such a lanthanideoxide/zirconium oxide as high-k dielectrics can be found in US PatentApplication Publication 2005/0077519 entitled “LanthanideOxide/Zirconium Oxide Atomic Layer Deposited Nanolaminate GateDielectrics,” which is herein incorporated by reference.

Lanthanide Oxide/Hafnium Oxide

The high-k dielectric can be provided by a lanthanide oxide/hafniumoxide nanolaminate, such as can be formed by forming a layer of hafniumoxide by atomic layer deposition and forming a layer of a lanthanideoxide by electron beam evaporation. According to various embodiments,the combined thickness of lanthanide oxide layers is limited to betweenabout 2 nm and about 10 nm. Multi-layers of hafnium oxide can be formed,where each layer of lanthanide oxide is limited to a thickness betweenabout 2 nm and 10 nm. Some embodiments limit the combined thickness ofhafnium oxide layers to a thickness between about 2 nm and about 10 nm.The lanthanide oxide can include Pr₂O₃, Nd₂O₃, Sm₂O₃, Gd₂O₃, and Dy₂O₃.The substrate temperature for the deposition can range between about100° C. to about 150° C. The hafnium oxide can be formed using a HfI₄precursor, and the lanthanide oxide can be formed on the layer ofhafnium oxide by electron beam evaporation.

Additional information regarding nanolaminates such a lanthanideoxide/hafnium oxide as high-k dielectrics can be found in US PatentApplication Publication 2005/0020017 entitled “Lanthanide Oxide/HafniumOxide Dielectric Layers,” which is herein incorporated by reference.

Lanthanide Oxide/Hafnium Oxide

The high-k dielectric can be provided by a lanthanide oxide/hafniumoxide nanolaminate. The hafnium oxide can be formed by chemical vapordeposition and the lanthanide oxide can be formed by electron beamevaporation. Forming the layer of hafnium oxide by chemical vapordeposition using precursors that do not contain carbon permits theformation of the dielectric layer without carbon contamination. Variousembodiments limit a combined thickness of lanthanide oxide layers to athickness ranging from about 2 nm to about 10 nm. Various embodimentsprovide a multilayer of lanthanide oxide, with each layer of lanthanideoxide having a thickness ranging from about 2 nm to about 10 nm. Variousembodiments limit a combined thickness of hafnium oxide layers to athickness ranging from about 2 nanometers to about 10 nanometers. Thelanthanide oxide can be selected from Pr₂O₃, Nd₂O₃, Sm₂O₃, Gd₂O₃, andDy₂O₃. The substrate can be maintained at a temperature ranging fromabout 100° C. to about 150° C. during electron beam deposition and thesubstrate can be maintained at a temperature ranging from about 200° C.to about 400° C. during chemical vapor deposition. The dielectric layercan be formed by forming a layer of hafnium oxide on a substrate bychemical vapor deposition using a Hf(NO₃)₄ precursor, and forming alayer of a lanthanide oxide on the layer of hafnium oxide by electronbeam evaporation.

Additional information regarding nanolaminates such a lanthanideoxide/hafnium oxide as high-k dielectrics can be found in US PatentApplication Publication 2004/0262700 entitled “Lanthanide Oxide/HafniumOxide Dielectric Layers,” which is herein incorporated by reference.

PrO_(X)/ZrO₂

The high-k dielectric can be provided by a PrO_(X)/ZrO₂ nanolaminate.The nanolaminate layered dielectric structure is formed by depositingpraseodymium by atomic layer deposition onto a substrate surface usingprecursor chemicals, followed by depositing zirconium onto the substrateusing precursor chemicals, and repeating to form the thin laminatestructure. The dielectric layer can be formed using either a reactionsequence atomic layer deposition, a metallo-organic chemical vapordeposition, or a combination thereof. The praseodymium oxide layerincludes forming an amorphous oxide including Pr₆O₁₁, Pr₂O₃, PrO₃, andPrO₂, and combinations thereof. The zirconium oxide layer can include anamorphous oxide including ZrO, ZrO₂, and combinations thereof.

Each individual one of the praseodymium oxide layers can be less than orequal to two monolayers in thickness, or can be a continuous monolayer.The resulting monolayer has a root mean square surface roughness that isless than one tenth of the layer thickness. The thickness of thepraseodymium oxide layer and the zirconium oxide layer can be selectedto provide the dielectric structure with a dielectric constant greaterthan 30. The dielectric film can be formed at a temperature of less than350° C. The dielectric film can be formed using a precursor materialcomprising a formula Pr(OCMe₂CH₂Me)₃.

Additional information regarding nanolaminates such a lanthanideoxide/hafnium oxide as high-k dielectrics can be found in U.S. patentapplication Ser. No. 11/010,766, filed Dec. 13, 2004 entitled “HybridALD-CVD of Pr_(X)O_(Y)/ZrO₂ Films as Gate Dielectrics,” which is hereinincorporated by reference.

Hf₃N₄/HfO₂

The high-k dielectric can be provided by a hafnium nitride(Hf₃N₄)/hafnium oxide (HfO₂) nanolaminate. At least one hafnium oxidelayer and at least one hafnium nitride layer form the nanolaminate. Boththe hafnium oxide and the hafnium nitride can be formed using atomiclayer deposition. The dielectric layer can include an amorphousdielectric that includes HfO₂, Hf₃N₄, and combinations thereof.

The hafnium oxide layer can be comprised of a plurality of individuallydeposited hafnium oxide layers, where each individual one of the hafniumoxide layers is less than or equal to two monolayers in thickness. Eachindividual one of the hafnium oxide layers can be a continuousmonolayer. Each individual one of the hafnium oxide layers can have athickness within a range from 1.3 to 1.5 Å. The resulting dielectriclayer can have a root mean square surface roughness that is less thanone tenth of the layer thickness. A ratio of a thickness of hafniumoxide to a thickness of hafnium nitride can be selected to result in adielectric constant of the dielectric film of greater than 20. Someembodiments separate the dielectric film from the substrate by adiffusion barrier. The dielectric film can be formed at a temperatureless than 300° C.

Hf[(CH₃)₂]₄ can be used as a precursor and water vapor can be used as areactant to form the hafnium oxide in a deposition process with atemperature between 250° C. to 300° C. HfCl₄ can be used as a precursorand water vapor can be used as a reactant to form the hafnium oxide in adeposition process with a temperature of approximately 300° C.Hf[(CH₃)₂]₄ can be used as a precursor and ammonia (NH₃) can be used asa reactant to form the hafnium oxide in a deposition process with atemperature of approximately 250° C. Various embodiments provide thehafnium nitride and hafnium oxide film as a continuous layer with a rootmean square surface roughness of less than 10 Å and a current leakagerate of less than 5×10⁻⁷ amps per cm² at an electric field strength of 1megavolt per cm.

Additional information regarding nanolaminates such a lanthanideoxide/hafnium oxide as high-k dielectrics can be found in U.S. patentapplication Ser. No. 11/063,717 filed Feb. 23, 2005 entitled “AtomicLayer Deposition of Hf₃N₄/HfO₂ Films as Gate Dielectrics,” which isherein incorporated by reference.

Zr₃N₄/ZrO₂

The high-k dielectric can be provided by a Zr₃N₄/ZrO₂ nanolaminate.Atomic layer deposition can be used to form at least one zirconium oxidelayer and at least one zirconium nitride layer. The dielectric layer caninclude an amorphous dielectric that includes ZrO₂, Zr₃N₄, andcombinations thereof. The zirconium oxide layer can be comprised of aplurality of individually deposited zirconium oxide layers, where eachindividual one of the zirconium oxide layers is less than or equal totwo monolayers in thickness. Each individual one of the zirconium oxidelayers can be a continuous monolayer with a step coverage of greaterthan 90% over 90 degree angle steps. In various embodiments, eachindividual one of the zirconium oxide layers has a thickness within arange from 1.3 to 1.5 Å. Some embodiments provide the dielectric layerwith a root mean square surface roughness that is less than one tenth ofthe layer thickness. A ratio of a thickness of zirconium oxide to athickness of zirconium nitride can be selected to result in a dielectricconstant of the dielectric film of greater than 20. A diffusion barriercan separate the dielectric film from the substrate. The dielectric filmcan be formed at a temperature of between 275° C. to 325° C. ZrI₄ can beused as a precursor, and water vapor and hydrogen peroxide can be usedas reactants to form zirconium oxide in a deposition process where thetemperature is between 325° C. to 500° C. ZrCl₄ can be used as aprecursor, and water vapor can be used as a reactant to form zirconiumoxide in a deposition process where the temperature is approximately300° C. Zr[(CH₃)₂]₄, can be used as a precursor and ammonia (NH₃) can beused as a reactant to form zirconium oxide in a deposition process wherethe temperature is approximately 250° C. The zirconium nitride andzirconium oxide film can each be a continuous layer having a root meansquare surface roughness of less than 5 Å and a current leakage rate ofless than 0.1×10⁻⁷ amps per cm² at an electric field strength of 1megavolt per cm.

Additional information regarding nanolaminates such a Zr₃N₄/ZrO₂ oxideas high-k dielectrics can be found in U.S. patent application Ser. No.11/058,563, filed Feb. 15, 2005 entitled “Atomic Layer Deposition ofZr₃N₄/ZrO₂ Films as Gate Dielectrics,” which is herein incorporated byreference.

TiO₂/CeO₂

The high-k dielectric can be provided by a TiO₂/CeO₂ nanolaminate usingALD processes.

Wafer Level

FIG. 3 illustrates a wafer 340, upon which the transistors with metalsubstituted gates can be fabricated according to embodiments of thepresent subject matter. A common wafer size is 8 inches in diameter.However, wafers are capable of being fabricated in other sizes, and thepresent subject matter is not limited to wafers of a particular size. Anumber of dies can be formed on a wafer. A die 341 is an individualpattern, typically rectangular, on a substrate that contains circuitryto perform a specific function. A semiconductor wafer typically containsa repeated pattern of such dies containing the same functionality. A dieis typically packaged in a protective casing (not shown) with leadsextending therefrom (not shown) providing access to the circuitry of thedie for communication and control.

System Level

FIG. 4 illustrates a simplified block diagram of a high-levelorganization of an electronic system that includes the transistor withthe metal-substituted gate, according to various embodiments. In variousembodiments, the system 450 is a computer system, a process controlsystem or other system that employs a processor and associated memory.The electronic system 450 has functional elements, including a processoror arithmetic/logic unit (ALU) 451, a control unit 452, a memory deviceunit 453 and an input/output (I/O) device 454. Generally such anelectronic system 450 will have a native set of instructions thatspecify operations to be performed on data by the processor 451 andother interactions between the processor 451, the memory device unit 453and the I/O devices 454. The control unit 452 coordinates all operationsof the processor 451, the memory device 453 and the I/O devices 454 bycontinuously cycling through a set of operations that cause instructionsto be fetched from the memory device 453 and executed. According tovarious embodiments, the memory device 453 includes, but is not limitedto, random access memory (RAM) devices, read-only memory (ROM) devices,and peripheral devices such as a floppy disk drive and a compact diskCD-ROM drive. As one of ordinary skill in the art will understand uponreading and comprehending this disclosure, any of the illustratedelectrical components are capable of being fabricated to include atransistor with a substituted gate in accordance with the presentsubject matter.

FIG. 5 illustrates a simplified block diagram of a high-levelorganization of an electronic system that includes transistors withmetal substituted gates, according to various embodiments. The system560 includes a memory device 561 which has an array of memory cells 562,address decoder 563, row access circuitry 564, column access circuitry565, read/write control circuitry 566 for controlling operations, andinput/output circuitry 567. The memory device 561 further includes powercircuitry 568, and sensors 569 for determining the state of the memorycells. The illustrated power circuitry 568 includes power supplycircuitry, circuitry for providing a reference voltage, circuitry forproviding the word line with pulses, and circuitry for providing the bitline with pulses. Also, as shown in FIG. 5, the system 560 includes aprocessor 570, or memory controller for memory accessing. The memorydevice receives control signals from the processor over wiring ormetallization lines. The memory device is used to store data which isaccessed via I/O lines. It will be appreciated by those skilled in theart that additional circuitry and control signals can be provided, andthat the memory device has been simplified. At least one of theprocessor or memory device includes the transistor with the metalsubstituted gate according to the present subject matter.

The illustration of system 560, as shown in FIG. 5, is intended toprovide a general understanding of one application for the structure andcircuitry of the present subject matter, and is not intended to serve asa complete description of all the elements and features of an electronicsystem. As one of ordinary skill in the art will understand, such anelectronic system can be fabricated in single-package processing units,or even on a single semiconductor chip, in order to reduce thecommunication time between the processor and the memory device.

Applications containing transistors with metal gates on high-kdielectrics, as described in this disclosure, include electronic systemsfor use in memory modules, device drivers, power modules, communicationmodems, processor modules, and application-specific modules, and mayinclude multilayer, multichip modules. Such circuitry can further be asubcomponent of a variety of electronic systems, such as a clock, atelevision, a cell phone, a personal computer, an automobile, anindustrial control system, an aircraft, and others.

This disclosure includes several processes, circuit diagrams, andstructures. The present invention is not limited to a particular processorder or logical arrangement. Although specific embodiments have beenillustrated and described herein, it will be appreciated by those ofordinary skill in the art that any arrangement which is calculated toachieve the same purpose may be substituted for the specific embodimentsshown. This application is intended to cover adaptations or variations.It is to be understood that the above description is intended to beillustrative, and not restrictive. Combinations of the aboveembodiments, and other embodiments, will be apparent to those of skillin the art upon reviewing the above description. The scope of thepresent invention should be determined with reference to the appendedclaims, along with the full scope of equivalents to which such claimsare entitled.

1. An integrated circuit structure, comprising: a substrate; a gatedielectric over the substrate; a carbon structure having a predeterminedthickness in contact with and over the gate dielectric; and a layer ofdesired gate material for a transistor in contact with and over thecarbon structure, the layer of desired gate material including apredetermined thickness corresponding to the predetermined thickness ofthe carbon structure to support a metal substitution process to replacethe carbon structure with the desired gate material.
 2. The structure ofclaim 1, wherein the gate dielectric includes a high-k gate dielectric.3. The structure of claim 1, wherein the desired gate material includesgold.
 4. The structure of claim 1, wherein the desired gate materialincludes silver.
 5. The structure of claim 1, wherein the desired gatematerial includes gold alloy.
 6. The structure of claim 1, wherein thedesired gate material includes silver alloy.
 7. The structure of claim1, wherein the desired gate material includes copper.
 8. The structureof claim 1, wherein the desired gate material includes platinum.
 9. Thestructure of claim 1, wherein the desired gate material includesrhenium.
 10. The structure of claim 1, wherein the desired gate materialincludes ruthenium.
 11. The structure of claim 1, wherein the desiredgate material includes rhodium.
 12. The structure of claim 1, whereinthe desired gate material includes nickel.
 13. The structure of claim 1,wherein the desired gate material includes osmium.
 14. The structure ofclaim 1, wherein the desired gate material includes palladium.
 15. Thestructure of claim 1, wherein the desired gate material includesiridium.
 16. The structure of claim 1, wherein the desired gate materialincludes cobalt.
 17. The structure of claim 1, wherein the desired gatematerial includes germanium.
 18. An integrated circuit structure,comprising: a substrate; a high-k gate dielectric over the substrate,the high-k gate dielectric having a dielectric constant above thedielectric constant of silicon; a carbon structure having apredetermined thickness in contact with and over the high-k gatedielectric; and a layer of metal in contact with and over the carbonstructure, the layer of metal including a predetermined thicknesscorresponding to the predetermined thickness of the carbon structure tosupport a metal substitution process to replace the carbon structurewith the metal to provide a metal gate over the high-k dielectric. 19.The structure of claim 18, wherein the high-k dielectric includes one ormore monolayers of a high-k dielectric material.
 20. The structure ofclaim 18, wherein the high-k dielectric includes a nanolaminate of twoor more high-k dielectrics.
 21. The structure of claim 18, wherein themetal gate material is selected from a group consisting of: gold, alloysof gold, silver, alloys of silver, platinum, rhenium, ruthenium,rhodium, nickel, osmium, palladium, iridium, cobalt, and germanium. 22.An integrated circuit structure, comprising: a substrate; a high-k gatedielectric in contact with the substrate, the high-k gate dielectrichaving a dielectric constant above the dielectric constant of silicon; asilicon-germanium structure having a predetermined thickness in contactwith the high-k gate dielectric, the silicon-germanium structureincluding a percentage of silicon and germanium; and a layer of metal incontact with the silicon-germanium structure, the layer of metalincluding a predetermined thickness corresponding to the predeterminedthickness of the silicon-germanium structure to support a metalsubstitution process to replace the silicon-germanium structure with themetal to provide a metal gate in contact with the high-k dielectric. 23.The structure of claim 22, wherein the metal gate includes aluminum. 24.The structure of claim 22, wherein the metal gate includes gold.
 25. Thestructure of claim 22, wherein the metal gate includes silver.
 26. Thestructure of claim 22, wherein the high-k dielectric includes monolayersof a high-k dielectric material.
 27. The structure of claim 22, whereinthe high-k dielectric includes a nanolaminate of at least two high-kdielectric materials.
 28. An integrated circuit structure, comprising: asubstrate; a high-k gate dielectric in contact with the substrate, thehigh-k gate dielectric having a dielectric constant above the dielectricconstant of silicon; a polysilicon structure having a predeterminedthickness in contact with the high-k gate dielectric; and a layer ofmetal in contact with the polysilicon structure, the layer of metalincluding a predetermined thickness corresponding to the predeterminedthickness of the polysilicon structure to support a metal substitutionprocess to replace the polysilicon structure with the metal to provide ametal gate in contact with the high-k dielectric.
 29. The structure ofclaim 28, wherein the metal gate includes aluminum.
 30. The structure ofclaim 28, wherein the metal gate includes gold.
 31. The structure ofclaim 28, wherein the metal gate includes silver.
 32. The structure ofclaim 28, wherein the high-k dielectric includes monolayers of a high-kdielectric material.
 33. The structure of claim 28, wherein the high-kdielectric includes a nanolaminate of at least two high-k dielectricmaterials.
 34. An integrated circuit structure, comprising: a substrate;a high-k gate dielectric in contact with the substrate, the high-k gatedielectric having a dielectric constant above the dielectric constant ofsilicon; a germanium structure having a predetermined thickness incontact with the high-k gate dielectric; and a layer of metal in contactwith the germanium structure, the layer of metal including apredetermined thickness corresponding to the predetermined thickness ofthe germanium structure to support a metal substitution process toreplace the germanium structure with the metal to provide a metal gateover the high-k dielectric.
 35. The structure of claim 34, wherein themetal gate includes aluminum.
 36. The structure of claim 34, wherein themetal gate includes gold.
 37. The structure of claim 34, wherein themetal gate includes silver.
 38. The structure of claim 34, wherein thehigh-k dielectric includes monolayers of a high-k dielectric material.39. The structure of claim 34, wherein the high-k dielectric includes ananolaminate of at least two high-k dielectric materials.